EP2980964B1 - Method for manufacturing sintered bearing - Google Patents

Method for manufacturing sintered bearing Download PDF

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Publication number
EP2980964B1
EP2980964B1 EP14774064.1A EP14774064A EP2980964B1 EP 2980964 B1 EP2980964 B1 EP 2980964B1 EP 14774064 A EP14774064 A EP 14774064A EP 2980964 B1 EP2980964 B1 EP 2980964B1
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EP
European Patent Office
Prior art keywords
powder
sintered
bearing
iron
copper
Prior art date
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EP14774064.1A
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German (de)
English (en)
French (fr)
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EP2980964A4 (en
EP2980964A1 (en
Inventor
Yoshinori Ito
Yousuke Sugai
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NTN Corp
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NTN Corp
NTN Toyo Bearing Co Ltd
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Priority claimed from JP2014007916A external-priority patent/JP6412314B2/ja
Priority claimed from JP2014008889A external-priority patent/JP6412315B2/ja
Application filed by NTN Corp, NTN Toyo Bearing Co Ltd filed Critical NTN Corp
Publication of EP2980964A1 publication Critical patent/EP2980964A1/en
Publication of EP2980964A4 publication Critical patent/EP2980964A4/en
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    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B06—GENERATING OR TRANSMITTING MECHANICAL VIBRATIONS IN GENERAL
    • B06B—METHODS OR APPARATUS FOR GENERATING OR TRANSMITTING MECHANICAL VIBRATIONS OF INFRASONIC, SONIC, OR ULTRASONIC FREQUENCY, e.g. FOR PERFORMING MECHANICAL WORK IN GENERAL
    • B06B1/00—Methods or apparatus for generating mechanical vibrations of infrasonic, sonic, or ultrasonic frequency
    • B06B1/10—Methods or apparatus for generating mechanical vibrations of infrasonic, sonic, or ultrasonic frequency making use of mechanical energy
    • B06B1/16—Methods or apparatus for generating mechanical vibrations of infrasonic, sonic, or ultrasonic frequency making use of mechanical energy operating with systems involving rotary unbalanced masses
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
    • B22F1/00—Metallic powder; Treatment of metallic powder, e.g. to facilitate working or to improve properties
    • B22F1/17—Metallic particles coated with metal
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
    • B22F3/00—Manufacture of workpieces or articles from metallic powder characterised by the manner of compacting or sintering; Apparatus specially adapted therefor ; Presses and furnaces
    • B22F3/12—Both compacting and sintering
    • B22F3/16—Both compacting and sintering in successive or repeated steps
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
    • B22F5/00—Manufacture of workpieces or articles from metallic powder characterised by the special shape of the product
    • B22F5/10—Manufacture of workpieces or articles from metallic powder characterised by the special shape of the product of articles with cavities or holes, not otherwise provided for in the preceding subgroups
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/16—Ferrous alloys, e.g. steel alloys containing copper
    • F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
    • F16—ENGINEERING ELEMENTS AND UNITS; GENERAL MEASURES FOR PRODUCING AND MAINTAINING EFFECTIVE FUNCTIONING OF MACHINES OR INSTALLATIONS; THERMAL INSULATION IN GENERAL
    • F16C—SHAFTS; FLEXIBLE SHAFTS; ELEMENTS OR CRANKSHAFT MECHANISMS; ROTARY BODIES OTHER THAN GEARING ELEMENTS; BEARINGS
    • F16C33/00—Parts of bearings; Special methods for making bearings or parts thereof
    • F16C33/02—Parts of sliding-contact bearings
    • F16C33/04—Brasses; Bushes; Linings
    • F16C33/06—Sliding surface mainly made of metal
    • F16C33/10—Construction relative to lubrication
    • F16C33/1025—Construction relative to lubrication with liquid, e.g. oil, as lubricant
    • F16C33/103—Construction relative to lubrication with liquid, e.g. oil, as lubricant retained in or near the bearing
    • F16C33/104—Construction relative to lubrication with liquid, e.g. oil, as lubricant retained in or near the bearing in a porous body, e.g. oil impregnated sintered sleeve
    • F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
    • F16—ENGINEERING ELEMENTS AND UNITS; GENERAL MEASURES FOR PRODUCING AND MAINTAINING EFFECTIVE FUNCTIONING OF MACHINES OR INSTALLATIONS; THERMAL INSULATION IN GENERAL
    • F16C—SHAFTS; FLEXIBLE SHAFTS; ELEMENTS OR CRANKSHAFT MECHANISMS; ROTARY BODIES OTHER THAN GEARING ELEMENTS; BEARINGS
    • F16C33/00—Parts of bearings; Special methods for making bearings or parts thereof
    • F16C33/02—Parts of sliding-contact bearings
    • F16C33/04—Brasses; Bushes; Linings
    • F16C33/06—Sliding surface mainly made of metal
    • F16C33/10—Construction relative to lubrication
    • F16C33/1095—Construction relative to lubrication with solids as lubricant, e.g. dry coatings, powder
    • F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
    • F16—ENGINEERING ELEMENTS AND UNITS; GENERAL MEASURES FOR PRODUCING AND MAINTAINING EFFECTIVE FUNCTIONING OF MACHINES OR INSTALLATIONS; THERMAL INSULATION IN GENERAL
    • F16C—SHAFTS; FLEXIBLE SHAFTS; ELEMENTS OR CRANKSHAFT MECHANISMS; ROTARY BODIES OTHER THAN GEARING ELEMENTS; BEARINGS
    • F16C33/00—Parts of bearings; Special methods for making bearings or parts thereof
    • F16C33/02—Parts of sliding-contact bearings
    • F16C33/04—Brasses; Bushes; Linings
    • F16C33/06—Sliding surface mainly made of metal
    • F16C33/12—Structural composition; Use of special materials or surface treatments, e.g. for rust-proofing
    • F16C33/128—Porous bearings, e.g. bushes of sintered alloy
    • F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
    • F16—ENGINEERING ELEMENTS AND UNITS; GENERAL MEASURES FOR PRODUCING AND MAINTAINING EFFECTIVE FUNCTIONING OF MACHINES OR INSTALLATIONS; THERMAL INSULATION IN GENERAL
    • F16C—SHAFTS; FLEXIBLE SHAFTS; ELEMENTS OR CRANKSHAFT MECHANISMS; ROTARY BODIES OTHER THAN GEARING ELEMENTS; BEARINGS
    • F16C33/00—Parts of bearings; Special methods for making bearings or parts thereof
    • F16C33/02—Parts of sliding-contact bearings
    • F16C33/04—Brasses; Bushes; Linings
    • F16C33/06—Sliding surface mainly made of metal
    • F16C33/14—Special methods of manufacture; Running-in
    • F16C33/145—Special methods of manufacture; Running-in of sintered porous bearings
    • H—ELECTRICITY
    • H02—GENERATION; CONVERSION OR DISTRIBUTION OF ELECTRIC POWER
    • H02K—DYNAMO-ELECTRIC MACHINES
    • H02K5/00—Casings; Enclosures; Supports
    • H02K5/04—Casings or enclosures characterised by the shape, form or construction thereof
    • H02K5/16—Means for supporting bearings, e.g. insulating supports or means for fitting bearings in the bearing-shields
    • H—ELECTRICITY
    • H02—GENERATION; CONVERSION OR DISTRIBUTION OF ELECTRIC POWER
    • H02K—DYNAMO-ELECTRIC MACHINES
    • H02K5/00—Casings; Enclosures; Supports
    • H02K5/04—Casings or enclosures characterised by the shape, form or construction thereof
    • H02K5/16—Means for supporting bearings, e.g. insulating supports or means for fitting bearings in the bearing-shields
    • H02K5/167—Means for supporting bearings, e.g. insulating supports or means for fitting bearings in the bearing-shields using sliding-contact or spherical cap bearings
    • H—ELECTRICITY
    • H02—GENERATION; CONVERSION OR DISTRIBUTION OF ELECTRIC POWER
    • H02K—DYNAMO-ELECTRIC MACHINES
    • H02K7/00—Arrangements for handling mechanical energy structurally associated with dynamo-electric machines, e.g. structural association with mechanical driving motors or auxiliary dynamo-electric machines
    • H02K7/06—Means for converting reciprocating motion into rotary motion or vice versa
    • H02K7/065—Electromechanical oscillators; Vibrating magnetic drives
    • H—ELECTRICITY
    • H02—GENERATION; CONVERSION OR DISTRIBUTION OF ELECTRIC POWER
    • H02K—DYNAMO-ELECTRIC MACHINES
    • H02K7/00—Arrangements for handling mechanical energy structurally associated with dynamo-electric machines, e.g. structural association with mechanical driving motors or auxiliary dynamo-electric machines
    • H02K7/08—Structural association with bearings
    • H02K7/083—Structural association with bearings radially supporting the rotary shaft at both ends of the rotor
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
    • B22F1/00—Metallic powder; Treatment of metallic powder, e.g. to facilitate working or to improve properties
    • B22F1/05—Metallic powder characterised by the size or surface area of the particles
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
    • B22F2998/00—Supplementary information concerning processes or compositions relating to powder metallurgy
    • B22F2998/10—Processes characterised by the sequence of their steps
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
    • B22F7/00—Manufacture of composite layers, workpieces, or articles, comprising metallic powder, by sintering the powder, with or without compacting wherein at least one part is obtained by sintering or compression
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C33/00—Making ferrous alloys
    • C22C33/02—Making ferrous alloys by powder metallurgy
    • C22C33/0207—Using a mixture of prealloyed powders or a master alloy
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C9/00—Alloys based on copper
    • F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
    • F16—ENGINEERING ELEMENTS AND UNITS; GENERAL MEASURES FOR PRODUCING AND MAINTAINING EFFECTIVE FUNCTIONING OF MACHINES OR INSTALLATIONS; THERMAL INSULATION IN GENERAL
    • F16C—SHAFTS; FLEXIBLE SHAFTS; ELEMENTS OR CRANKSHAFT MECHANISMS; ROTARY BODIES OTHER THAN GEARING ELEMENTS; BEARINGS
    • F16C2202/00—Solid materials defined by their properties
    • F16C2202/50—Lubricating properties
    • F16C2202/52—Graphite
    • F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
    • F16—ENGINEERING ELEMENTS AND UNITS; GENERAL MEASURES FOR PRODUCING AND MAINTAINING EFFECTIVE FUNCTIONING OF MACHINES OR INSTALLATIONS; THERMAL INSULATION IN GENERAL
    • F16C—SHAFTS; FLEXIBLE SHAFTS; ELEMENTS OR CRANKSHAFT MECHANISMS; ROTARY BODIES OTHER THAN GEARING ELEMENTS; BEARINGS
    • F16C2202/00—Solid materials defined by their properties
    • F16C2202/50—Lubricating properties
    • F16C2202/54—Molybdenum disulfide
    • F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
    • F16—ENGINEERING ELEMENTS AND UNITS; GENERAL MEASURES FOR PRODUCING AND MAINTAINING EFFECTIVE FUNCTIONING OF MACHINES OR INSTALLATIONS; THERMAL INSULATION IN GENERAL
    • F16C—SHAFTS; FLEXIBLE SHAFTS; ELEMENTS OR CRANKSHAFT MECHANISMS; ROTARY BODIES OTHER THAN GEARING ELEMENTS; BEARINGS
    • F16C2204/00—Metallic materials; Alloys
    • F16C2204/60—Ferrous alloys, e.g. steel alloys
    • F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
    • F16—ENGINEERING ELEMENTS AND UNITS; GENERAL MEASURES FOR PRODUCING AND MAINTAINING EFFECTIVE FUNCTIONING OF MACHINES OR INSTALLATIONS; THERMAL INSULATION IN GENERAL
    • F16C—SHAFTS; FLEXIBLE SHAFTS; ELEMENTS OR CRANKSHAFT MECHANISMS; ROTARY BODIES OTHER THAN GEARING ELEMENTS; BEARINGS
    • F16C2240/00—Specified values or numerical ranges of parameters; Relations between them
    • F16C2240/40—Linear dimensions, e.g. length, radius, thickness, gap
    • F16C2240/48—Particle sizes
    • F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
    • F16—ENGINEERING ELEMENTS AND UNITS; GENERAL MEASURES FOR PRODUCING AND MAINTAINING EFFECTIVE FUNCTIONING OF MACHINES OR INSTALLATIONS; THERMAL INSULATION IN GENERAL
    • F16C—SHAFTS; FLEXIBLE SHAFTS; ELEMENTS OR CRANKSHAFT MECHANISMS; ROTARY BODIES OTHER THAN GEARING ELEMENTS; BEARINGS
    • F16C2380/00—Electrical apparatus
    • F16C2380/26—Dynamo-electric machines or combinations therewith, e.g. electro-motors and generators
    • H—ELECTRICITY
    • H02—GENERATION; CONVERSION OR DISTRIBUTION OF ELECTRIC POWER
    • H02K—DYNAMO-ELECTRIC MACHINES
    • H02K7/00—Arrangements for handling mechanical energy structurally associated with dynamo-electric machines, e.g. structural association with mechanical driving motors or auxiliary dynamo-electric machines
    • H02K7/06—Means for converting reciprocating motion into rotary motion or vice versa
    • H02K7/061—Means for converting reciprocating motion into rotary motion or vice versa using rotary unbalanced masses

Definitions

  • the present invention relates to a method for manufacturing a sintered bearing.
  • a sintered bearing is a porous member having innumerable internal pores, and is usually used in the condition that the internal pores are immersed with a lubricant fluid (for example, lubricating oil).
  • a lubricant fluid for example, lubricating oil
  • the lubricating oil retained in the internal pores of the sintered bearing seeps onto the inner peripheral surface (bearing surface) of the sintered bearing as the temperature rises.
  • the seeped lubricating oil forms an oil film in the bearing gap between the bearing surface of the sintered bearing and the outer peripheral surface of the shaft, and the shaft is relatively rotatably supported.
  • Patent Document 1 describes an iron-copper-based sintered bearing which is mainly composed of iron and copper, and which is obtained by compacting and sintering a copper-coated iron powder, in which an iron powder is coated with copper in an amount of greater than or equal to 10 mass% and less than 30 mass%, and the granularity is less than or equal to 80 mesh.
  • JP 2008 232230 A discloses a process to produce a Fe-Cu based sintered bearing using iron powder plated with Cu. Alternatively such Cu plated layer can be replaced with CuSn alloy.
  • US 2003/215349 A1 discloses a process to produce highly dense sintered compact using partially alloy Fe powder with Mn, Mo,Cr,Ni Cu or V.
  • US 2012/177528 A1 discloses a process to produe an oil impregnated bearing wherein one of the starting powder material is fully alloy Fe-Cu one.
  • an object of the present invention is to strengthen the sintered bearing and to improve the wear resistance of the bearing surface. Another object of the present invention is to provide a vibration motor capable of exerting the high rotation performance stably for a long time at low cost.
  • a vibration motor functions as a vibrator for informing incoming call or reception of an e-mail in a portable terminal such as a cellular phone, and is so designed that vibration is produced in the entire terminal by supporting axially-spaced two parts of a shaft to which a weight (decentered weight) is attached, by a cylindrical sintered bearing having a bearing surface on the inner periphery, and by rotating the shaft with a motor part, as described, for example, in Patent Documents 2 and 3.
  • the sintered bearing is fixed to the inner periphery of a housing formed, for example, of a metal material.
  • the weight swingably rotates along the whole surface of the bearing surface of the sintered bearing under the influence of the weight. That is, in this type of vibration motor, the shaft rotates while its center is decentered in every direction with respect to the bearing center of the sintered bearing.
  • the use condition of the sintered bearing is already severer than that of the sintered bearing of normal use (for example, a sintered bearing for a spindle motor), and the bearing surface is easily worn out. Therefore, increasing the rotation speed of the motor further promotes wear of the bearing surface, and further increases the rotation fluctuation caused by wear of the bearing surface.
  • the present invention devised in consideration of such circumstances is a method for manufacturing a sintered bearing as defined in the appended claim 1.
  • the low-melting-point metal powder contained in the green compact melts as the green compact is sintered in the sintering step. Since the low-melting-point metal has high wettability against copper, it is possible to achieve secure bonding between an iron structure and a copper structure or between copper structures of neighboring diffusion alloyed powder grains by liquid phase sintering.
  • the neck strength between the iron structure and the copper structure is further increased because the melted low-melting-point metal diffuses therein. Therefore, it is possible to manufacture a high-strength sintered compact (sintered bearing) having excellent wear resistance of bearing surface and high radial crushing strength (for example, 300 MPa or higher) without using a powder of expensive metal such as Ni or Mo, or by sintering the green compact by a low-temperature sintering in which the green compact is heated (sintered) at a relatively low temperature.
  • the increased wear resistance of the bearing surface makes it possible to prevent rotation fluctuation caused by wear of the bearing surface. If the sintered bearing does not have a sufficient radial crushing strength, the bearing surface deforms (circularity, cylindricity and so on of the bearing surface decreases) especially when the sintered bearing is press-fitted into the housing inner periphery. Therefore, it is necessary to additionally execute a shape correcting process such as sizing after press fitting, and to finish the bearing surface to have an appropriate shape.
  • the sintering temperature (heating temperature) of the green compact can be set, for example, at greater than or equal to 820°C and less than or equal to 900°C.
  • the carbon contained in the gas diffuses into an iron structure, so that it is possible to obtain a sintered compact in which the iron structure is composed of a two-phase structure of a ferrite phase and a pearlite phase.
  • the sintered compact in which all the iron structure is formed of a ferrite phase is applicable, however, when the iron structure is formed of the aforementioned two-phase structure, the sintered compact contains a hard pearlite phase, and the wear resistance of the bearing surface can be further improved.
  • the copper powder contained in the green compact does not melt, and the copper is not diffused in the iron structure in association with sintering. Therefore, an appropriate amount of copper structure (bronze phase) is formed on the surface of the sintered compact. Therefore, it is possible to obtain a bearing surface having excellent initial conformability with the shaft, and a small frictional coefficient.
  • a diffusion alloyed powder in which a copper powder having a mean grain diameter of greater than or equal to 5 ⁇ m and less than 20 ⁇ m is partially diffused in an iron powder and containing 10 to 30% by mass of Cu.
  • a base powder contains a diffusion alloyed powder having a large grain diameter exceeding a mean grain diameter of 106 ⁇ m, a coarse pore is easily formed inside the sintered compact, resulting that required wear resistance, radial crushing strength and so on of the bearing surface cannot be necessarily ensured. Therefore, it is preferable to use a diffusion alloyed powder having an average grain size of less than or equal to 145 mesh (mean grain diameter of less than or equal to 106 ⁇ m).
  • a diffusion alloyed powder having an average grain size of less than or equal to 145 mesh (mean grain diameter of less than or equal to 106 ⁇ m).
  • the base powder in which 0.5 to 3.0% by mass of a tin powder as a low-melting-point metal powder is mixed, and 0.3 to 1.5% by mass of a graphite powder as a solid lubricant powder is mixed. This makes it possible to stably mass produce sintered bearings capable of appropriately achieving the operation and the effect as described above.
  • a reduced iron powder can be used as the iron powder constituting the diffusion alloyed powder (Fe-Cu diffusion alloyed powder).
  • the iron powder for example, an atomized iron powder can be used besides the reduced iron powder, however, since the reduced iron powder is in the form of a sponge having internal pores (porous), the powder is softer than the atomized iron powder, and is excellent in compaction property. Therefore, it is possible to increase the green compact strength even at low density, and to prevent occurrence of a break or a crack. Also since the reduced iron powder is in the form of a sponge, it is more excellent in oil retention compared with the atomized iron powder.
  • an oil-impregnating step for impregnating a lubricating oil into internal pores of the sintered compact can be provided.
  • a lubricating oil having a kinematic viscosity at 40°C ranging from 10 to 50 mm 2 /s, or a liquid grease based on an oil (lubricating oil) having a kinematic viscosity at 40°C ranging from 10 to 50 mm 2 /s can be impregnated into internal pores of the sintered compact.
  • the sintered bearing produced according to the method of the present invention can be used in a motor, particularly, in a vibration motor.
  • a vibration motor has a shaft, a motor part for rotationally driving the shaft, a sintered bearing having a bearing surface on its inner periphery and rotatably supporting the shaft, a weight provided on the shaft, and a housing in which the sintered bearing is fixed by press-fitting on its inner periphery, and vibration is generated by eccentrically rotating the shaft with respect to the bearing center by means of the weight.
  • a sintered bearing (not part of the claimed invention) for a vibration motor which is formed of a sintered compact containing iron as a main ingredient and copper as a second major ingredient, and having a radial crushing strength of greater than or equal to 300 MPa can be used.
  • a sintered compact containing iron which is low in price and excellent in mechanical strength as a main ingredient, and copper which is excellent in sliding properties such as initial conformability with the shaft as a second major ingredient, it is possible to ensure high rotation performance without incurring special cost increase even when the rotation speed of the motor is increased or the unbalanced load is increased.
  • the sintered bearing having a radial crushing strength of greater than or equal to 300 MPa even when the sinteredbearing is fixed to the housing inner periphery by press-fitting, deformation of the bearing surface caused by press-fitting, and reduction in circularity, cylindricity or the like of the bearing surface can be prevented as much as possible. Therefore, it is no longer necessary to additionally execute a process for finishing the bearing surface to have a specified shape and accuracy for the sintered bearing fixed to the housing inner periphery.
  • press-fitting which is a convenient fixing means without any problem as a means for fixing the sintered bearing to the housing.
  • the sintered bearing having a radial crushing strength of greater than or equal to 300 MPa makes it possible to prevent deformation or the like of the bearing surface as much as possible even when a mobile terminal into which the vibration motor is incorporated falls, and a large impact value is applied to the vibration motor (sintered bearing). As described above, it is possible to provide a vibration motor capable of exerting high rotation performance stably over a long term, at low cost.
  • the sintered bearing a sintered compact obtained by molding and sintering a base powder containing a diffusion alloyed powder prepared by partially diffusing a copper powder in an iron powder, a low-melting-point metal powder, and a solid lubricant powder can be used.
  • a reduced iron powder is preferably used.
  • the diffusion alloyed powder having an average grain size of less than or equal to 145 mesh (mean grain diameter of less than or equal to 106 ⁇ m) is preferably used.
  • the sintered bearing can be obtained from a base powder in which a tin powder is used as the low-melting-point metal powder and a graphite powder is used as the solid lubricant powder.
  • the sintered bearing can be formed of a sintered compact composed of 10 to 30% by mass of Cu, 0.5 to 3.0% by mass of Sn, 0.3 to 1.5% by mass of C, and the iron and inevitable impurities as the balance.
  • the iron structure of the sintered compact is formed based on a soft ferrite phase, it is possible to weaken the aggression of the bearing surface with respect to the shaft, so that it becomes possible to suppress wear of the shaft.
  • the iron structure based on a ferrite phase can be obtained by sintering a green compact, for example, at a temperature of less than or equal to 900°C at which iron and carbon (graphite) do not react with each other.
  • the iron structure based on a ferrite phase includes a structure that is entirely a ferrite phase, and an iron structure in which a pearlite phase which is harder than the ferrite phase is present in the grain boundary of the ferrite phase. In this manner, by forming the pearlite phase in the grain boundary of the ferrite phase, it is possible to improve the wear resistance of the bearing surface in comparison with the case where the iron structure is formed solely of the ferrite phase.
  • the ratio can be determined, for example, by respective area proportions of the ferrite phase and the pearlite phase in an arbitrary section of the sintered compact.
  • porosity of the superficial part of the sintered compact in particular, porosity of the superficial part including the bearing surface is preferably 5 to 20%.
  • the superficial part used herein means a region spanning from the surface to 100 ⁇ m deep.
  • the sintered bearing can be a so-called sintered oil-impregnatedbearing in which a lubricating oil is impregnated into internal pores of the sintered compact, and in this case, the lubricating oil having a kinematic viscosity at 40°C ranging from 10 to 50 mm 2 /s is preferably used.
  • a liquid grease based on a lubricating oil having a kinematic viscosity at 40°C ranging from 10 to 50 mm 2 /s may be impregnated into the sintered compact.
  • a sintered bearing can be arranged on both sides of the axial direction of the motor part.
  • one sintered bearing is disposed between the weight and the motor part, and an axial dimension of the one sintered bearing can be made larger than an axial dimension of the other sintered bearing.
  • the sintered bearing produced according to the method of the present invention is used while it is incorporated into a motor, for example, in a vibration motor, it is possible to provide a motor with excellent reliability and durability at low cost. Even when the rotation speed of the vibration motor is increased or the unbalanced load is increased, high rotation performance can be exerted stably for a long term.
  • FIG. 1 is a schematic sectional view of an essential part of a typical vibration motor.
  • a vibration motor 1 exemplarily illustrated in the drawing includes a motor part M having a rotor magnet, a stator coil, and so on, a substantially cylindrical housing 2 formed of metal or resin, a ring-shaped sintered bearings 4 (41, 42) disposed at two points in the axial direction spaced from each other and fixed to the inner periphery of the housing 2 by press-fitting, and a shaft 3 inserted on the inner periphery of the sintered bearings 4 (41, 42).
  • the shaft 3 is adapted to be rotationally driven at a rotation speed of greater than or equal to 10000 rpm by the motor part M disposed between the two sintered bearings 41, 42.
  • the shaft 3 is formed of a metal material such as stainless steel, and has a diameter of less than or equal to 2 mm (preferably less than or equal to 1.0 mm).
  • One end part of the shaft 3 is provided with a weight W integrally or separately for making the shaft 3 eccentrically rotate with respect to the sintered bearing 4.
  • a gap width of a gap (bearing gap) formed between an outer peripheral surface 3a of the shaft 3 and a bearing surface 4a of the sintered bearing 4 is set, for example, at about 4 ⁇ m for either side (by radius) .
  • a lubricating oil e.g., synthetic hydrocarbon-based lubricating oil having a kinematic viscosity at 40°C ranging from 10 to 50 mm 2 /s is impregnated.
  • a lubricating oil having such a low viscosity is selected and used for impregnation into internal pores of the a sintered bearing 4 so as to prevent increase in rotation torque while ensuring the rigidity of the oil film formed in the bearing gap.
  • a liquid grease based on an oil having a kinematic viscosity at 40°C ranging from 10 to 50 mm 2 /s may be impregnated in place of the aforementioned lubricating oil.
  • the vibration motor 1 having such a configuration, when the motor part M is energized and the shaft 3 rotates relatively to the sintered bearing 4, the lubricating oil retained in the internal pores of the sintered bearing 4 seeps onto the bearing surface 4a as the temperature rises.
  • the seeped lubricating oil forms an oil film in the bearing gap between the facing outer peripheral surface 3a of the shaft 3 and the bearing surface 4a of the sintered bearing 4, so that the shaft 3 is supported by the sintered bearing 4 in a relatively rotatable manner.
  • the shaft 3 rotates swingably along the whole surface of the bearing surface 4a under the influence of the weight W provided on its one end. That is, the shaft 3 rotates in the condition that a center Oa is decentered in every direction with respect to a center Ob of the sintered bearings 4 (41, 42) as shown in Fig. 2 .
  • the axial length and the thickness in the radial direction are selected different between the two sintered bearings 41, 42 (area of the bearing surface 4a).
  • the area of the bearing surface 4a of the sintered bearing 41 on the side closer to the weight W is set larger than the area of the bearing surface 4a of the sintered bearing 42 on the side farther from the weight W.
  • the vibration motor 1 may be provided with a seal member for sealing an opening of the housing 2.
  • the sintered bearing 4 described in the above is formed of an iron-copper based sintered compact containing iron as a main ingredient and 10 to 30% by mass of copper, and has a radial crushing strength of greater than or equal to 300 MPa.
  • the sintered bearing 4 as described above is produced by conducting (A) base powder generating step P1, (B) compacting step P2, (C) sintering step P3, (D) sizing step P4 and (E) oil-impregnating step P5 in sequence.
  • A base powder generating step P1
  • B compacting step P2
  • C sintering step P3
  • D sizing step P4
  • E oil-impregnating step P5
  • a base powder 10 which is a material for preparation of the sintered bearing 4 is uniformed by mixing later-described plural kinds of powder.
  • the base powder 10 used in the present embodiment is a mixed powder containing a diffusion alloyed powder, which is also called partially alloyed powder or partially pre-alloyed powder, as a main material, a low-melting-point metal powder, and a solid lubricant powder.
  • a variety of molding lubricants for example, a lubricant for improving release properties may be added to the base powder 10 as is necessary.
  • each powder will be described in detail.
  • a Fe-Cu diffusion alloyed powder prepared by partially diffusing a copper powder 13 on the surface of an iron powder 12 is used, and in the present embodiment, a Fe-Cu diffusion alloyed powder prepared by partially diffusing a large number of copper powder grains 13 having a mean grain diameter smaller than that of the iron powder grain 12 on the surface of the iron powder grain 12 is used.
  • the diffused part of the diffusion alloyed powder forms a Fe-Cu alloy, and as shown in the partial enlarged view in Fig. 4 , the alloy part has such a crystalline structure that an iron atom 12a and a copper atom 13a are mutually bound and arrayed.
  • the diffusion alloyed powder 11 only grains having an average grain size of less than or equal to 145 mesh (mean grain diameter of less than or equal to 106 ⁇ m) are used.
  • the apparent density decreases and the powder becomes more likely to float as its grain diameter decreases. Therefore, when the diffusion alloyed powder 11 having a small grain diameter is abundantly contained in the base powder, the filling rate of the base powder with respect to a molding die (cavity) decreases in the later-described compacting step P2, and it becomes difficult to stably obtain a green compact of a specified shape and density. Specifically, the inventors found that the aforementioned problem is likely to arise when 25% by mass or more of the diffusion alloyed powder 11 having a grain diameter of less than or equal to 45 ⁇ m is contained.
  • the diffusion alloyed powder 11 it is preferable to select and use the diffusion alloyed powder 11 having an average grain size of less than or equal to 145 mesh (mean grain diameter of less than or equal to 106 ⁇ m), and not containing 25% by mass or more of grains having an average grain size of less than or equal to 350 mesh (mean grain diameter 45 ⁇ m).
  • the mean grain diameter can be measured by a laser diffraction scattering method (using, for example, SALD31000 available from Shimadzu Corporation) including irradiating a group of grains with laser beam, and determining a grain size distribution and a mean grain diameter by calculation from the intensity distribution pattern of the diffracted and scattered light emitted therefrom (a mean grain diameter of later-described powder can also be determined in a similar manner).
  • a laser diffraction scattering method using, for example, SALD31000 available from Shimadzu Corporation
  • the iron powder 12 forming the diffusion alloyed powder 11 a known iron powder such as a reduced iron powder, an atomized iron powder or the like can be used without any problem, and in the present embodiment, a reduced iron powder is used.
  • the reduced iron powder is also called a sponge iron powder because it has an irregular shape approximate to a sphere, and is spongy (porous) with internal pores.
  • the iron powder 12 used herein preferably has a mean grain diameter ranging from 20 ⁇ m to 106 ⁇ m, and more preferably has a mean grain diameter ranging from 38 ⁇ m to 75 ⁇ m.
  • a generally used irregular-shaped or arborized copper powder can be widely used, and for example, an electrolytic copper powder, an atomized copper powder or the like is used.
  • an atomized copper powder having a large number of recesses and protrusions on the surface, and forming an irregular shape approximate to a sphere as the entire grain, and having excellent moldability is used.
  • the copper powder 13 having a smaller grain diameter than the iron powder 12 is used, and specifically, the copper powder 13 having a mean grain diameter of greater than or equal to 5 ⁇ m and less than or equal to 20 ⁇ m (preferably less than 20 ⁇ m) is used.
  • the proportion of Cu in each diffusion alloyed powder grain 11 is 10 to 30% by mass (preferably 22 to 26% by mass), and is equivalent to the mass proportion of copper contained in the sintered compact 4" obtained in the sintering step P3 (strictly, a mass proportion of copper when the sintered compact 4" does not contain Sn and C). That is, in the present embodiment, a simple copper powder or iron powder is not mixed in the base powder 10. Although a simple copper powder or iron powder may be mixed into the base powder, if a simple copper powder is mixed, it becomes difficult to improve the wear resistance of the bearing surface 4a. Therefore, an indentation (recess) is more likely to be formed on the bearing surface 4a, for example, when the bearing surface 4a collides with the shaft 3 as the shaft 3 rotates. If a simple iron powder is mixed, it becomes difficult to obtain a sintered compact (sintered bearing) having a desired radial crushing strength. Therefore, it is preferable not to mix a simple copper powder or iron powder into the base powder.
  • metal powder having a melting point of less than or equal to 700°C for example, powder of tin, zinc, phosphorus or the like is used.
  • the tin powder (atomized tin powder) 14 having a mean grain diameter ranging from 5 to 63 ⁇ m is preferably used, and the tin powder (atomized tin powder) 14 having a mean grain diameter ranging from 20 to 45 ⁇ m is more preferably used.
  • the tin powder 14 is mixed at 0.5 to 3.0% by mass in the base powder 10.
  • the solid lubricant one or two or more kinds of powder of graphite, molybdenum disulfide or the like can be used.
  • a graphite powder in particular, a flake graphite powder is used in consideration of the cost.
  • the graphite powder is mixed at 0.3 to 1.5% by mass in the base powder 10.
  • a ring-shaped green compact 4 ' having a shape approximate to the sintered bearing 4 as illustrated in Fig. 1 or the like is obtained.
  • the molding die 20 mainly has a core 21, an upper punch 22, a lower punch 23, and a die 24, which are coaxially disposed.
  • the molding die 20 is set, for example, in a die set of a cam type molding pressing machine.
  • the upper punch 22 is relatively moved to approach the lower punch 23, and the base powder 10 is compacted by an appropriate pressing pressure (which is set depending on the shape and size of the green compact to be molded) .
  • an appropriate pressing pressure which is set depending on the shape and size of the green compact to be molded.
  • a green compact 4' having a shape approximate to the sintered bearing 4 is obtained.
  • the upper punch 22 is elevated and the lower punch 23 is elevated, and the green compact 4' is discharged outside the cavity 25.
  • the diffusion alloyed powder 11, the tin powder 14, and the graphite powder are uniformly dispersed in the green compact 4'.
  • the powder since a reduced iron powder is used as the iron powder 12 forming the diffusion alloyed powder 11, the powder is softer than the diffusion alloyed powder using an atomized iron powder, and is excellent in compaction property. Therefore, it is possible to increase the strength of the green compact 4' even with low density, and to prevent occurrence of a break or a crack in the green compact 4'.
  • the green compact 4' is subjected to a sintering process to obtain a sintered compact.
  • the sintering condition in the present embodiment is such that carbon contained in the graphite powder does not react with iron (carbon will not be diffused).
  • iron carbon will not be diffused.
  • there is a transformation point at 723°C and over this point, reaction between iron and carbon starts to form a pearlite phase ( ⁇ Fe) in the iron structure.
  • reaction between carbon (graphite) and iron starts at a temperature exceeding 900°C, and a pearlite phase is formed.
  • the pearlite phase has a high hardness of greater than or equal to HV300, if this is present in the iron structure of the sintered bearing 4, it is possible to increase the wear resistance of the bearing surface 4a, and suppress wear of the bearing surface 4a under high surface pressure, to thereby elongate the bearing service life.
  • the green compact 4' is sintered in such a condition that a pearlite phase is contained in the iron structure after sintering (iron structure of the sintered compact), more specifically, the iron structure after sintering is structured by a two-phase structure consisting of a relatively soft ferrite phase (less than or equal to HV200) and a relatively hard pearlite phase. Since the pearlite phase having high hardness strongly attacks the counter member, wear of the shaft 3 can be advanced if the pearlite phase is present abundantly in the iron structure of the sintered bearing 4. For preventing this, as illustrated in Fig.
  • the pearlite phase ⁇ Fe is so controlled that it is present (scattered) in the grain boundary of the ferrite phase ⁇ Fe.
  • the "grain boundary” used herein means both a grain boundary formed between powder grains, and a grain boundary formed in a powder grain.
  • a deposition amount of the pearlite phase ⁇ Fe principally depends on the sintering temperature and the atmospheric gas. Therefore, to obtain an iron structure formed of a two-phase structure consisting of a pearlite phase ⁇ Fe and a ferrite phase ⁇ Fe wherein the pearlite phase ⁇ Fe is such a degree that it is just present in a grain boundary of the ferrite phase ⁇ Fe, the heating temperature (sintering temperature) of the green compact 4' is set at greater than or equal to 820°C and less than or equal to 900°C.
  • the sintering atmosphere is a carbon-containing gas atmosphere including an endothermic gas (RX gas) generated by mixing a liquified petroleum gas such as butane or propane and air, and thermally decomposing the mixed gas with a Ni catalyst, natural gas or the like.
  • RX gas endothermic gas
  • carbon contained in the gas is diffused into iron at the time of sintering, and hence the pearlite phase ⁇ Fe of the degree as described above can be formed.
  • the green compact 4' is heated and sintered at a temperature exceeding 900°C, carbon contained in the graphite powder reacts with iron, and the pearlite phase ⁇ Fe is excessively formed in the iron structure of the sintered compact.
  • the sintering temperature of the green compact 4' is set at less than or equal to 900°C.
  • the molding lubricants such as a fluid lubricant, the molding lubricants are volatilized with sintering.
  • the sintered compact 4" obtained by heating and sintering the green compact 4' in the above condition contains 10 to 30% by mass (preferably 22 to 26% by mass) of Cu, 0.5 to 3.0% by mass (preferably 1.0 to 3.0% by mass) of Sn, 0.3 to 1.5% by mass (preferably 0.5 to 1.0% by mass) of C, and iron and inevitable impurities as the balance.
  • the metal structure of the sintered compact 4" is mostly formed of iron (iron structure), so that it has excellent mechanical strength.
  • the sintered compact 4" contains a certain amount of copper in the metal structure, the bearing surface 4a having excellent initial conformability with respect to the shaft 3 can be obtained.
  • the sintering temperature of the green compact 4' is set lower than the melting point of copper (1083°C)
  • the copper powder 13 contained in the green compact 4' does not melt during sintering, and copper does not diffuse in iron (iron structure) during sintering. Therefore, an appropriate amount of copper structure containing a bronze phase is formed on the surface (bearing surface 4a) of the sintered compact 4". Also, free graphite is exposed on the surface of the sintered compact 4". Accordingly, it is possible to obtain the bearing surface 4a having excellent initial conformability with the shaft 3 and a small frictional coefficient.
  • the sintered compact 4" sintered bearing 4 having high mechanical strength can be obtained by increasing the mixing amount of Sn, an excessive amount of Sn leads increase in coarse pores and causes deterioration in the wear resistance of the bearing surface 4a. For this reason, the aforementioned mixing proportion (mixing proportion of about 10% by mass with respect to the mixing proportion of Cu) is selected.
  • an iron structure based on iron and a copper structure based on copper are formed.
  • every iron structure and copper structure in the sintered compact 4" is formed based on the diffusion alloyed powder 11.
  • the diffusion alloyed powder since part of the copper powder is diffused in the iron powder, it is possible to obtain high neck strength between the iron structure and the copper structure after sintering. Also during sintering of the green compact 4' , the tin powder 14 in the green compact 4' melts and wets the surface of the copper powder 13 forming the diffusion alloyed powder 11.
  • the sintered compact 4" and thus the sintered bearing 4 having high mechanical strength (radial crushing strength), specifically a radial crushing strength of greater than or equal to 300 MPa even by sintering at low temperature as described above without using expensive metal powder such as Ni and Mo. Also, it is possible to improve the wear resistance of the bearing surface 4a by hardening the bearing surface 4a.
  • the ferrite phase ⁇ Fe, the pearlite phase ⁇ Fe and so on are represented by a shade of color. Specifically, the color is thickened in the order of ferrite phase ⁇ Fe, bronze phase 16, Fe-Cu-Sn alloy 17, and pearlite phase ⁇ Fe.
  • the diffusion alloyed powder 11 since a powder having an average grain size of less than or equal to 145 mesh (mean grain diameter of less than or equal to 106 ⁇ m) is used as the diffusion alloyed powder 11, it is possible to uniform the porous structure of the sintered compact 4" and to prevent generation of coarse pores . Therefore, it is possible to densify the sintered compact 4", and to further improve the wear resistance and the radial crushing strength of the bearing surface 4a.
  • the porosity of the superficial part can be 5 to 20%.
  • the porosity can be determined, for example, by image analysis of an area proportion of pore parts in an arbitrary section of the sintered compact 4".
  • Densification of the superficial part in this manner makes it possible to obtain the bearing surface 4a having relatively small surface aperture rate, specifically, the bearing surface 4a having a surface aperture rate of greater than or equal to 5% and less than or equal to 20% .
  • the surface aperture rate of the bearing surface 4a is less than 5%, it becomes difficult to make a necessary and sufficient amount of the lubricating oil seep into the bearing gap (oil film forming ability is insufficient), and a merit as the sintered bearing 4 cannot be obtained.
  • the base powder used for obtaining the sintered compact 4" is based on the diffusion alloyed powder 11 prepared by partially diffusing the copper powder 13 on the surface of the iron powder 12, it is possible to prevent segregation of copper which is problematic in an existent iron-copper-based sintered bearing.
  • the sintering condition of the green compact 4' can be set so that the iron structure after sintering is formed of a two-phase structure consisting of a ferrite phase ⁇ Fe and a pearlite phase ⁇ Fe, or so that every iron structure after sintering is a ferrite phase ⁇ Fe.
  • the heating temperature of the green compact 4' is set at greater than or equal to 800°C (preferably 820°C) and less than or equal to 880°C, and a gas atmosphere not containing carbon (hydrogen gas, nitrogen gas, argon gas and so on) or a vacuum is selected as the sintering atmosphere.
  • the sintered compact 4" obtained in the manner as described above is subjected to sizing in the sizing step P4.
  • the sintered compact 4" is finishedtoa final shape and dimension .
  • the sizing can be conducted as necessary, and need not to be necessarily conducted. That is, if each part of the sintered compact 4" obtained in the sintering step P3 is finished into a desired shape, dimension or the like, the sizing step P4 may be omitted.
  • the sintered bearing 4 (sintered compact 4") obtained in the manufacturing process of the present embodiment has a radial crushing strength of greater than or equal to 300 MPa, and this value of radial crushing strength is greater than or equal to twice that of an existent iron-copper-based sintered bearing.
  • the density of the sintered bearing 4 of the present embodiment is 6.8 ⁇ 0.3 g/cm 3 , which is higher than the density of an existent iron-copper-based sintered bearing (about 6.6 g/cm 3 ).
  • the sintered bearing 4 obtained in the manufacturing method according to the present invention is formed of the sintered compact 4" having high radial crushing strength (radial crushing strength of greater than or equal to 300 MPa), even when the sintered bearing 4 is fixed to the inner periphery of the housing 2 by press-fitting, the bearing surface 4a does not deform in conformance with the inner periphery surface shape of the housing 2, and the circularity, cylindricity or the like of the bearing surface 4a can be stably maintained even after attachment.
  • a microphotograph of the superficial part of the sintered bearing 4 obtained in the manufacturing method according to the present invention is shown in Fig. 8
  • a microphotograph of a superficial part of a sintered bearing according to the art described in Patent Document 1 (hereinafter, referred to as "copper-coated iron powder bearing") is shown in Fig. 9 .
  • the porous structure of the superficial part is compact in comparison with that of the copper-coated iron powder bearing.
  • the porosity of the superficial part of the sintered bearing 4 is 13.6%
  • the porosity of the superficial part of the copper-coated iron powder bearing is about 25.5%.
  • One of the reasons of such difference is insufficient neck strength between iron structure and copper structure because the copper film merely closely adheres to the iron powder in the copper-coated iron powder.
  • part of the iron structure or copper structure may be formed of a simple iron powder or a simple copper powder by adding either one or both of the simple iron powder and the simple copper powder to the base powder.
  • the proportion of the diffusion alloyed powder in the base powder is preferably greater than or equal to 50% by mass .
  • an appropriate mixing proportion of the solid lubricant powder in the base powder is 0.3 to 1.5% by mass.
  • the mixing proportion of the low-melting-point metal powder in the base powder is 0.5 to 5.0% by mass.
  • This mixing proportion is preferably set at about 10% by mass of the total amount of the copper powder in the base powder (sum of a copper powder in the diffusion alloyed powder and a separately added simple copper powder) .
  • the base powder is formed of a simple iron powder or a simple copper powder (or both simple powders), and inevitable impurities as the balance.
  • a so-called warm compaction in which the green compact 4' is compacted while at least one of the molding die 20 and the base powder 10 is heated, or a die wall lubricating compaction in which the green compact 4' is compacted while a lubricant is applied to the molding surface of the molding die 20 (the surface defining the cavity 25) may be employed.
  • the vibration motor 1 described above is of the shaft rotating type in which the shaft 3 is rotative and the sintered bearing 4 is stationary
  • the vibration motor 1 may be of a shaft stationary type in which the shaft 3 is stationary and the sintered bearing 4 is rotative
  • the sintered bearing 4 obtained in the manufacturing method according to the present invention can be preferably applied to the vibration motor 1 of such a shaft stationary type.
  • the bearing surface 4a of the sintered bearing 4 can be provided with a dynamic pressure generating part such as a dynamic pressure groove. This makes it possible to increase the rigidity of the oil film formed in the bearing gap, and thus to further increase the rotation accuracy.
  • the sintered bearing 4 obtained in the manufacturing method according to the present invention has various uses including use for supporting a principal axis of a high-speed motor with a large unbalanced load, use as a bearing for rotatably supporting a shaft while it is incorporated into various motors, as well as use for a vibration motor because of its high mechanical strength and excellent wear resistance of the bearing surface 4a.

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Families Citing this family (11)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP5442145B1 (ja) * 2012-10-24 2014-03-12 Ｎｔｎ株式会社 焼結軸受
JPWO2015025576A1 (ja) * 2013-08-20 2017-03-02 日立オートモティブシステムズ株式会社 内燃機関用電動式空気流量制御装置
JP6625321B2 (ja) * 2014-11-28 2019-12-25 Ntn株式会社 動圧軸受及びその製造方法
KR102118595B1 (ko) 2015-04-24 2020-06-04 한온시스템 주식회사 양두 사판식 압축기 및 실린더 블록의 제작방법
CN105871101B (zh) * 2016-05-23 2018-03-16 杭州万辰机电科技有限公司 高速永磁电机
JP6817094B2 (ja) * 2016-07-29 2021-01-20 株式会社ダイヤメット 鉄銅基焼結含油軸受及びその製造方法
US10697495B2 (en) 2016-07-29 2020-06-30 Diamet Corporation Iron-copper-based oil-impregnated sintered bearing and method for manufacturing same
JP6864459B2 (ja) * 2016-10-18 2021-04-28 株式会社ダイヤメット 焼結含油軸受およびその製造方法
JP2019167569A (ja) * 2018-03-22 2019-10-03 Ntn株式会社 機械部品およびその製造方法
CN111761051B (zh) * 2020-06-10 2022-07-19 鞍钢(鞍山)冶金粉材有限公司 一种粉末冶金用含铜铁粉及其制备方法
CN114907901B (zh) * 2022-05-31 2022-12-16 中国科学院兰州化学物理研究所 一种无铅铜合金自润滑材料和泵马达双金属缸体及其制备方法

Citations (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US20030215349A1 (en) * 2002-02-28 2003-11-20 Hitachi Unisia Automotive, Ltd. Production method of high density iron based forged part

Family Cites Families (51)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPS5137606B2 (zh) 1971-10-12 1976-10-16
JPS613569A (ja) 1984-06-18 1986-01-09 Nippon Denki Kanji Syst Kk ランレングス符号化方法
DE3860288D1 (de) * 1987-05-05 1990-08-09 Interatom Verfahren zur herstellung von poroesen lagerschalen fuer gasstatische lager.
JPS63290245A (ja) * 1987-05-22 1988-11-28 Nissan Motor Co Ltd 耐摩耗性鉄基焼結合金
JPS63297502A (ja) 1987-05-29 1988-12-05 Kobe Steel Ltd 粉末冶金用高強度合金鋼粉及びその製造方法
JPH01275735A (ja) * 1988-04-27 1989-11-06 Isamu Kikuchi 焼結合金材およびその製造法
JP2551981B2 (ja) * 1988-09-14 1996-11-06 大同メタル工業 株式会社 複層鉄銅鉛系合金軸受材料
US5395807A (en) 1992-07-08 1995-03-07 The Carborundum Company Process for making silicon carbide with controlled porosity
JPH0820836A (ja) 1994-07-11 1996-01-23 Pooraito Kk 焼結含油軸受およびその製造方法
JP3484674B2 (ja) 1994-09-21 2004-01-06 同和鉄粉工業株式会社 粉末冶金用鉄基銅複合粉末の製造方法
EP0739991B1 (en) * 1995-04-25 2000-11-29 Kawasaki Steel Corporation Iron-base powder mixture for powder metallurgy and manufacturing method therefor
JPH0995759A (ja) 1995-09-29 1997-04-08 Heiwa Sangyo Kk 焼結含油軸受とその製造方法
US5941646A (en) * 1996-12-25 1999-08-24 Ntn Corporation Hydrodynamic type porous oil-impregnated bearing and bearing device
JPH1150103A (ja) 1997-07-29 1999-02-23 Kawasaki Steel Corp 粉末冶金用鉄粉の製造方法
GB2333779A (en) 1997-08-07 1999-08-04 Porite Corp Composite metal powder for sintered bearing, and sintered oil-retaining bearing
JPH11117044A (ja) 1997-10-13 1999-04-27 Mitsubishi Materials Corp 初期なじみ性のすぐれた遊離黒鉛析出型鉄系焼結材料製軸受
JPH11256206A (ja) * 1998-03-06 1999-09-21 Mabuchi Motor Co Ltd 小型モータ及びその焼結合金製含油軸受の製造方法
JP3932394B2 (ja) 1999-04-09 2007-06-20 ポーライト株式会社 焼結含油軸受およびその製造方法
JP2001003123A (ja) 1999-06-18 2001-01-09 Hitachi Powdered Metals Co Ltd 含油軸受用焼結合金およびその製造方法
JP4234865B2 (ja) * 1999-10-28 2009-03-04 オイレス工業株式会社 鉄系焼結摺動部材ならびにその製造方法
JP2001178100A (ja) 1999-12-16 2001-06-29 Shicoh Eng Co Ltd 振動モータ
JP2001251393A (ja) 2000-03-07 2001-09-14 Shicoh Eng Co Ltd 携帯無線通信機
JP3651420B2 (ja) 2000-08-31 2005-05-25 Ｊｆｅスチール株式会社 粉末冶金用合金鋼粉
JP3939931B2 (ja) * 2001-03-23 2007-07-04 大同メタル工業株式会社 銅系複層摺動材料
JP2002349575A (ja) 2001-05-29 2002-12-04 Asmo Co Ltd 焼結含油軸受及びその製造方法
JP2003184882A (ja) 2001-12-13 2003-07-03 Pooraito Kk 焼結含油軸受材
JP4365080B2 (ja) * 2002-10-31 2009-11-18 出光興産株式会社 焼結含油軸受油組成物及び焼結含油軸受ユニット
CN2648688Y (zh) * 2003-09-03 2004-10-13 深圳市双环全新机电有限公司 空心杯直流电机
JP4380274B2 (ja) * 2003-09-10 2009-12-09 日立粉末冶金株式会社 鉄銅系焼結含油軸受用合金の製造方法
JP4515824B2 (ja) * 2004-05-27 2010-08-04 Ｎｔｎ株式会社 高精度すべり軸受
JP5147184B2 (ja) 2005-01-27 2013-02-20 株式会社豊田中央研究所 鉄基焼結合金およびその製造方法
GB2437216A (en) 2005-01-31 2007-10-17 Komatsu Mfg Co Ltd Sintered material, iron-based sintered sliding material and process for producing the same
KR100722602B1 (ko) * 2005-09-16 2007-05-28 삼성전기주식회사 박형의 정류자 이탈방지체를 구비한 진동모터
JP2007169736A (ja) 2005-12-22 2007-07-05 Jfe Steel Kk 粉末冶金用合金鋼粉
KR101460573B1 (ko) * 2006-03-24 2014-11-20 엔티엔 가부시키가이샤 유체 베어링 장치
JP2008078537A (ja) * 2006-09-25 2008-04-03 Matsushita Electric Ind Co Ltd コンデンサ
JP2008099355A (ja) * 2006-10-06 2008-04-24 Seiko Instruments Inc モータ用軸受装置及び振動モータ
WO2008082353A1 (en) * 2006-12-29 2008-07-10 Höganäs Ab Powder, method of manufacturing a component and component
JP4886545B2 (ja) * 2007-02-22 2012-02-29 日立粉末冶金株式会社 焼結含油軸受およびその製造方法
JP2008232230A (ja) 2007-03-19 2008-10-02 Nippon Densan Corp 焼結軸受、軸受装置および軸受装置の製造方法
JP2010071350A (ja) * 2008-09-17 2010-04-02 Nippon Densan Corp 流体動圧軸受機構、モータ、記録ディスク駆動装置およびスリーブの製造方法
JP5247329B2 (ja) * 2008-09-25 2013-07-24 日立粉末冶金株式会社 鉄系焼結軸受およびその製造方法
KR101533458B1 (ko) 2008-10-23 2015-07-03 두산인프라코어 주식회사 내마모성이 향상된 슬라이딩 베어링 및 그 제조방법
JP5640315B2 (ja) 2009-02-06 2014-12-17 新日本理化株式会社 動圧流体軸受用又は焼結含油軸受用潤滑油組成物
KR101615147B1 (ko) * 2009-03-19 2016-04-25 엔티엔 가부시키가이샤 소결 금속 베어링 및 이 베어링을 구비한 유체 동압 베어링 장치
JP2011094167A (ja) * 2009-10-27 2011-05-12 Diamet:Kk 鉄銅系焼結摺動部材およびその製造方法
JP5675090B2 (ja) 2009-12-21 2015-02-25 株式会社ダイヤメット 焼結含油軸受及びその製造方法
JP5318018B2 (ja) 2010-03-30 2013-10-16 トヨタ自動車株式会社 焼結含油軸受
JP5619550B2 (ja) 2010-09-27 2014-11-05 Ntn株式会社 焼結軸受及びこれを備えた流体動圧軸受装置、並びに焼結軸受の製造方法
WO2013042664A1 (ja) 2011-09-22 2013-03-28 Ntn株式会社 焼結軸受およびその製造方法
JP5442145B1 (ja) 2012-10-24 2014-03-12 Ｎｔｎ株式会社 焼結軸受

Patent Citations (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US20030215349A1 (en) * 2002-02-28 2003-11-20 Hitachi Unisia Automotive, Ltd. Production method of high density iron based forged part

Non-Patent Citations (2)

* Cited by examiner, † Cited by third party
Title
ASTM STANDARDS: "Standard Test Method for Radial Crushing Strength, K, of Powder Metallurgy (P/M) Bearings and Structural Materials", 30 November 2005 (2005-11-30), XP055383144, Retrieved from the Internet <URL:ftp://185.72.26.245/Astm/1/Section%2002/ASTM0205/PDF/B939.pdf> [retrieved on 20170620] *
SHANMUGAM S ET AL: "Ring rupture strength and hardness of sintered hot-forged 1.5Mo alloyed carbon steels", JOURNAL OF MATERIALS PROCESSING TECHNOLOGY, ELSEVIER, NL, vol. 209, no. 7, 1 April 2009 (2009-04-01), pages 3426 - 3430, XP026076675, ISSN: 0924-0136, [retrieved on 20080807], DOI: 10.1016/J.JMATPROTEC.2008.07.043 *

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US10536048B2 (en) 2020-01-14
WO2014156856A1 (ja) 2014-10-02
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CN110043564A (zh) 2019-07-23
US20160301279A1 (en) 2016-10-13

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